WO2013187197A1 - アーク溶接構造部材の製造法 - Google Patents

アーク溶接構造部材の製造法 Download PDF

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Publication number
WO2013187197A1
WO2013187197A1 PCT/JP2013/064196 JP2013064196W WO2013187197A1 WO 2013187197 A1 WO2013187197 A1 WO 2013187197A1 JP 2013064196 W JP2013064196 W JP 2013064196W WO 2013187197 A1 WO2013187197 A1 WO 2013187197A1
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WIPO (PCT)
Prior art keywords
gas
welding
arc
plating layer
plated steel
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PCT/JP2013/064196
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English (en)
French (fr)
Japanese (ja)
Inventor
和昭 細見
延時　智和
朝田　博
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日新製鋼株式会社
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Priority to CA2874217A priority Critical patent/CA2874217A1/en
Priority to BR112014029946-3A priority patent/BR112014029946B1/pt
Application filed by 日新製鋼株式会社 filed Critical 日新製鋼株式会社
Priority to KR20147027115A priority patent/KR20150024302A/ko
Priority to MX2014010630A priority patent/MX362408B/es
Priority to US14/406,569 priority patent/US20150136741A1/en
Priority to SG11201406046YA priority patent/SG11201406046YA/en
Priority to NZ629861A priority patent/NZ629861A/en
Priority to RS20171171A priority patent/RS56575B1/sr
Priority to EP13803668.6A priority patent/EP2862662B1/en
Priority to MYPI2014703682A priority patent/MY181348A/en
Priority to CN201380022431.1A priority patent/CN104334308B/zh
Priority to AU2013275476A priority patent/AU2013275476B2/en
Priority to RU2015100899A priority patent/RU2635581C2/ru
Publication of WO2013187197A1 publication Critical patent/WO2013187197A1/ja
Priority to PH12014502019A priority patent/PH12014502019A1/en
Priority to AU2017204060A priority patent/AU2017204060B2/en

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    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/23—Arc welding or cutting taking account of the properties of the materials to be welded
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/001—Interlayers, transition pieces for metallurgical bonding of workpieces
    • B23K35/004—Interlayers, transition pieces for metallurgical bonding of workpieces at least one of the workpieces being of a metal of the iron group
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/38—Selection of media, e.g. special atmospheres for surrounding the working area
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K35/00—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting
    • B23K35/22—Rods, electrodes, materials, or media, for use in soldering, welding, or cutting characterised by the composition or nature of the material
    • B23K35/38—Selection of media, e.g. special atmospheres for surrounding the working area
    • B23K35/383—Selection of media, e.g. special atmospheres for surrounding the working area mainly containing noble gases or nitrogen
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/16—Arc welding or cutting making use of shielding gas
    • B23K9/173—Arc welding or cutting making use of shielding gas and of a consumable electrode
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B32—LAYERED PRODUCTS
    • B32B—LAYERED PRODUCTS, i.e. PRODUCTS BUILT-UP OF STRATA OF FLAT OR NON-FLAT, e.g. CELLULAR OR HONEYCOMB, FORM
    • B32B15/00—Layered products comprising a layer of metal
    • B32B15/01—Layered products comprising a layer of metal all layers being exclusively metallic
    • B32B15/013—Layered products comprising a layer of metal all layers being exclusively metallic one layer being formed of an iron alloy or steel, another layer being formed of a metal other than iron or aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C18/00—Alloys based on zinc
    • C22C18/04—Alloys based on zinc with aluminium as the next major constituent
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/12—Ferrous alloys, e.g. steel alloys containing tungsten, tantalum, molybdenum, vanadium, or niobium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C23—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; CHEMICAL SURFACE TREATMENT; DIFFUSION TREATMENT OF METALLIC MATERIAL; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL; INHIBITING CORROSION OF METALLIC MATERIAL OR INCRUSTATION IN GENERAL
    • C23C—COATING METALLIC MATERIAL; COATING MATERIAL WITH METALLIC MATERIAL; SURFACE TREATMENT OF METALLIC MATERIAL BY DIFFUSION INTO THE SURFACE, BY CHEMICAL CONVERSION OR SUBSTITUTION; COATING BY VACUUM EVAPORATION, BY SPUTTERING, BY ION IMPLANTATION OR BY CHEMICAL VAPOUR DEPOSITION, IN GENERAL
    • C23C2/00—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor
    • C23C2/04—Hot-dipping or immersion processes for applying the coating material in the molten state without affecting the shape; Apparatus therefor characterised by the coating material
    • C23C2/06—Zinc or cadmium or alloys based thereon
    • B—PERFORMING OPERATIONS; TRANSPORTING
    • B23—MACHINE TOOLS; METAL-WORKING NOT OTHERWISE PROVIDED FOR
    • B23K—SOLDERING OR UNSOLDERING; WELDING; CLADDING OR PLATING BY SOLDERING OR WELDING; CUTTING BY APPLYING HEAT LOCALLY, e.g. FLAME CUTTING; WORKING BY LASER BEAM
    • B23K9/00—Arc welding or cutting
    • B23K9/235—Preliminary treatment

Definitions

  • the present invention relates to a method for manufacturing an arc welded structure member having excellent resistance to molten metal embrittlement cracking formed by using a molten Zn—Al—Mg plated steel sheet member for one or both members to be joined.
  • Hot-dip galvanized steel sheets have good corrosion resistance and are used in a wide range of applications including building and automobile parts. Among them, the hot-dip Zn—Al—Mg-based steel sheet maintains excellent corrosion resistance for a long period of time, and therefore the demand is increasing as a substitute for the conventional hot-dip galvanized steel sheet.
  • the plated layer of the hot-dip Zn—Al—Mg-based plated steel sheet has a primary Al phase or a primary Al phase in a Zn / Al / Zn 2 Mg ternary eutectic matrix. It has a metal structure in which a Zn single phase is dispersed, and the corrosion resistance is improved by Al and Mg. Since a dense and stable corrosion product containing Mg in particular is uniformly formed on the surface of the plated layer, the corrosion resistance of the plated layer is remarkably improved as compared with the hot dip galvanized steel sheet.
  • the metal in the plating layer melts on the surface of the surrounding base material (plating original sheet) through which the arc has passed.
  • the alloy of the plating layer has a liquidus temperature lower than the melting point of Zn (about 420 ° C.) and maintains a molten state for a relatively long time.
  • the solidification end temperature is about 335 ° C.
  • Molten metal derived from the Zn-Al-Mg plating layer melted on the surface of the base metal reduces the Al concentration as the Al component reacts with the underlying Fe at an early stage and is consumed as an Fe-Al alloy layer.
  • the composition close to that of the Zn—Mg binary system is obtained, but even with a Zn-3 mass% Mg alloy, the solidification end temperature is 360 ° C., which is lower than the melting point of Zn, 420 ° C. Therefore, in the case of a Zn—Al—Mg plated steel sheet, the time during which the metal of the plated layer melted during arc welding stays on the surface of the base material while maintaining the liquid phase is longer than that of the galvanized steel sheet.
  • Patent Document 4 discloses a technique of imparting resistance to molten metal embrittlement cracking by applying a steel plate whose ferrite crystal grain boundary is reinforced by addition of B to a plating original plate.
  • Patent Document 5 discloses a technique of suppressing molten metal embrittlement cracking by filling Zn, Al, and Mg during arc welding by filling a flux added with TiO 2 and FeO into the outer sheath of a welding wire. .
  • the method of cutting and removing the plating layer and the method of using a special welding wire are accompanied by a great increase in cost.
  • the technique of using B-added steel for the plating base plate reduces the degree of freedom in selecting the steel type.
  • molten metal embrittlement cracking may not be sufficiently prevented, and a drastic arc welding structure using a Zn-Al-Mg based steel sheet is essential. It is not a measure to prevent molten metal embrittlement cracking.
  • the present invention is excellent in resistance to molten metal embrittlement in an arc welded structure member using a Zn—Al—Mg plated steel plate member without being restricted by the steel type of the plating base plate and a significant increase in cost. It aims at providing what has fracturing ability.
  • the plating layer disappears once by evaporation in the vicinity of the weld bead during gas shielded arc welding, but after the arc passes, the plating layer metal is in a molten state at a position slightly away from the bead. It has been confirmed that the phenomenon of immediately spreading to the above disappeared portion occurs. If this wetting spread is suppressed and cooling is completed while maintaining the state of evaporative disappearance, the penetration of the plating layer component into the base metal is avoided at a position close to the welding beat, and the molten metal embrittlement crack is It can be effectively prevented.
  • the above-described wetting and spreading in the Zn—Al—Mg-based plated steel sheet member is remarkably reduced by reducing the concentration of CO 2 that is usually mixed in the shielding gas by about 20% by volume. It was found to be suppressed.
  • the allowable upper limit of the CO 2 concentration can be managed as a function of welding heat input. Furthermore, it has been found that when the plate thickness of the Zn—Al—Mg-based plated steel plate member used is thin, the tolerance of the upper limit of CO 2 concentration increases. The present invention has been completed based on such findings.
  • the above object is to manufacture a welded structural member by joining steel materials by gas shielded arc welding, and at least one member to be joined is a molten Zn—Al—Mg based plated steel plate member, and Ar gas is used as a shielding gas.
  • Arc welding using a gas satisfying the following formula (2) in relation to the welding heat input Q (J / cm), in which the CO 2 concentration is represented by the following formula (1), based on He gas or Ar + He mixed gas This is achieved by a method for manufacturing a structural member.
  • the “hot-dipped Zn—Al—Mg-based plated steel sheet member” is a member made of a molten Zn—Al—Mg-based plated steel sheet, or a member formed by using it as a raw material.
  • the welding heat input Q can be, for example, in the range of 2000 to 12000 J / cm.
  • the molten Zn—Al—Mg-based plated steel sheet member uses a plating original sheet having a thickness of 2.6 mm or less (for example, 1.0 to 2.6 mm)
  • the following formula (2) is used instead.
  • Equation (3) can be applied. 0 ⁇ C CO2 ⁇ 205Q ⁇ 0.32 (3)
  • the welding heat input Q is more preferably in the range of 2000 to 4500 J / cm, for example.
  • the molten Zn—Al—Mg based steel sheet is, for example, mass%, Al: 1.0 to 22.0%, Mg: 0.05 to 10.0%, Ti: 0 to 0.10%, B: Those having a plating layer of 0 to 0.05%, Si: 0 to 2.0%, Fe: 0 to 2.5%, the balance Zn and unavoidable impurities are suitable targets.
  • the plating adhesion amount per one side is, for example, 20 to 250 g / m 2 .
  • an arc welded structure using a molten Zn—Al—Mg-based plated steel sheet member that is inherently susceptible to molten metal embrittlement cracking has excellent resistance to molten metal embrittlement cracking. It became possible to realize stably without increasing the cost. Since the allowable upper limit of the CO 2 concentration in the shielding gas has been clarified according to the welding heat input, the benefits of blending CO 2 (such as the suppression of oxidation around the weld bead using the reducing action of CO generated by the arc) ) To the maximum.
  • the steel type of the plating base plate there is no particular restriction on the steel type of the plating base plate, and it is not necessary to adopt a steel type to which a special element is added as a measure against molten metal embrittlement cracking. Even when a high-strength steel plate is applied, excellent melt metal embrittlement cracking resistance can be obtained. In addition, the degree of freedom for the part shape is great. Therefore, the present invention is widely used in the widespread use of Zn-Al-Mg-plated steel sheet arc welded structural members, including automotive arc welded structural members using high-tensile steel sheets, which are expected to increase in the future. It contributes.
  • FIG. 1 schematically shows a cross section of a torch and a base material during gas shielded arc welding.
  • the welding torch 31 advances in the direction of the arrow while forming an arc 35 on the surface of the base material 1.
  • a shield gas 34 is blown out from the periphery of the electrode 33 and the welding wire 32 positioned at the center of the welding torch 31 to protect the arc 35 and the surface of the base material 1 exposed to high temperatures from the atmosphere.
  • a part of the base material 1 melted by the heat input from the arc 35 is rapidly solidified after the welding torch 31 passes and forms a weld bead 2 made of weld metal.
  • the shield gas 34 needs to be a non-oxidizing gas.
  • an inert gas such as Ar which Ar + CO 2 mixed gas of CO 2 were mixed for about 20 vol% is employed.
  • a part of CO 2 in the shielding gas 34 is considered to be separated into CO and O 2 by the plasma arc 35, and the CO exerts a reducing action to suppress oxidation of the weld bead and its surroundings. Thereby, it is thought that the corrosion-resistant fall in a welding part is reduced.
  • FIG. 2 schematically illustrates the cross-sectional structure of the welded portion of the lap fillet welded joint.
  • This type of welded joint by arc welding is frequently used for automobile chassis.
  • a base material 1 and a base material 1 ′ which are steel plate members, are arranged so as to overlap each other, a weld bead 2 is formed on the surface of the base material 1 and an end surface of the base material 1 ′, and both members are joined.
  • the broken lines in the figure represent the surface position of the base material 1 and the end face position of the base material 1 'before welding.
  • the intersection of the base metal surface and the weld bead is called the “bead toe”.
  • the bead toe portion of the base material 1 is indicated by reference numeral 3.
  • FIG. 3 to 5 schematically show an enlarged cross-sectional structure of a portion corresponding to the vicinity of the bead toe 3 shown in FIG.
  • FIG. 3 schematically shows a cross-sectional state in the vicinity of a high-temperature weld immediately after the arc passes during gas shielded arc welding of a Zn—Al—Mg-based steel sheet.
  • the surface of the base material 1 was covered with the uniform plating layer 7 through the Fe—Al-based alloy layer 6 at the stage before welding, but the metal of the plating layer was near the bead toe 3 due to the passage of the arc. Evaporates and disappears (plating layer evaporation region 9).
  • the original plating layer 7 is melted to become the Zn—Al—Mg based molten metal 8, but has not disappeared due to evaporation.
  • the original plating layer 7 exists without melting.
  • the thicknesses of the Zn—Al—Mg molten metal 8 and the plating layer 7 are exaggerated.
  • FIG. 4 schematically shows a cross-sectional structure of a conventional Zn—Al—Mg-based plated steel sheet arc welded structural member obtained by cooling from the state of FIG.
  • the Zn—Al—Mg based molten metal reference numeral 8 in FIG. 3 wets and spreads in the “plating layer evaporation region” (reference numeral 9 in FIG. 3) formed once the plating layer disappears during welding, and the base material 1
  • the entire surface up to the bead toe 3 is covered with the Zn—Al—Mg alloy layer 5.
  • the portion of the Zn—Al—Mg based alloy layer 5 formed by solidification of the Zn—Al—Mg based molten metal (reference numeral 8 in FIG. 3) is referred to as a molten solidified region 10, and the original plating layer 7 remains and is formed.
  • the portion of the Zn—Al—Mg-based alloy layer 5 is referred to as a plating layer unmelted region 11.
  • the bead toe 3 is usually a melt-solidified region 10 as shown in FIG.
  • the liquidus temperature of the Zn—Al—Mg based molten metal 8 is low as described above, the surface portion of the base material 1 that becomes the molten and solidified region 10 after cooling becomes Zn—Al in the cooling process after welding. -The contact time with the Mg-based molten metal is relatively long. Since tensile stress is generated in the portion of the base material 1 near the bead toe due to cooling after welding, the Zn—Al—Mg based molten metal component tends to enter the crystal grain boundary. The said component which penetrate
  • FIG. 5 schematically shows a cross-sectional structure of a Zn—Al—Mg-based plated steel sheet arc welded structural member according to the present invention obtained by cooling from the state of FIG.
  • a gas having a reduced CO 2 concentration or a CO 2 -free gas is used as the shielding gas.
  • the surface of the base material 1 in the “plating layer evaporation region” (reference numeral 9 in FIG. 3) where the plating layer disappeared during welding is oxidized due to a weak reduction action by the shielding gas, and is quickly covered with a thin oxide film. Conceivable.
  • this oxide film inhibits the wetting with the Zn—Al—Mg based molten metal (reference numeral 8 in FIG. 3), thereby suppressing the wetting and spreading of the Zn—Al—Mg based molten metal.
  • the plating layer evaporation region 9 remains after cooling. That is, the surface of the base material 1 near the bead toe 3 is finished to cool without coming into contact with the Zn—Al—Mg-based molten metal, and intrusion of the molten metal component into the base material 1 at that portion is avoided. Is done. Therefore, excellent molten metal embrittlement cracking resistance is imparted without depending on the steel type of the base material 1.
  • a gas having a reduced CO 2 concentration or a gas not containing CO 2 is used as the shielding gas, so that the weld bead and its surroundings are more easily oxidized than in the prior art.
  • a molten Zn—Al—Mg-based plated steel sheet member as a member to be joined, not only the plating layer surface but also the corrosion resistance of the exposed part of the steel substrate in the vicinity of the welded part is improved. That is, in addition to the anticorrosive effect by Zn, the corrosion product derived from the Zn—Al—Mg based metal exhibits excellent protective properties, so that the long-term corrosion resistance is improved, and the gas or CO2 with reduced CO 2 concentration 2. Corrosion resistance degradation due to the use of an additive-free gas does not become apparent during normal use.
  • plating layer evaporation region length The length from the bead toe 3 of the plating layer evaporation region 9 remaining after cooling is referred to as “plating layer evaporation region length” in this specification, and is indicated by the symbol L in FIG.
  • plating layer evaporation region length Most of the molten metal embrittlement cracks that are a problem with Zn-Al-Mg-plated steel sheet arc welded structural members are very close to the bead toe 3, specifically less than 0.3 mm from the bead toe. It has been confirmed that As a result of various studies, if the plating layer evaporation region length is 0.3 mm or more, the molten metal embrittlement cracking resistance is greatly improved, and if it is 0.4 mm or more, it is more preferable.
  • the plating layer evaporation region length can be controlled in the range of 0.3 to 2.0 mm by adjusting the shield gas composition as described later.
  • the surface of the base material in which the plating layer in the vicinity of the welded portion has evaporated and disappeared is prevented from being excessively activated.
  • Zn—Al—Mg based molten metal present in the bead is prevented from spreading to the bead toes.
  • the above-mentioned which has a wider allowable upper limit, instead of the above formula (2) Even if the expression (3) is applied, the length of the plating layer evaporation region can be controlled in the range of 0.3 to 2.0 mm.
  • the thickness of at least one member to be joined is a plate thickness.
  • CO in the shielding gas according to the welding heat input Q (J / cm) represented by the above formula (1) CO 2 concentration adjusting method of shielding gas to adjust 2 concentration so as to satisfy the following formula (3) are disclosed. 0 ⁇ C CO2 ⁇ 205Q ⁇ 0.32 (3)
  • C CO2 is CO 2 concentration of the shielding gas (vol%).
  • the CO 2 concentration in the shielding gas may be adjusted within the range satisfying the above equation (2) and the above equation (3) depending on the plate thickness conditions, but from the viewpoint of stabilizing the arc, the CO 2 concentration of 5% by volume or more. Is more effective. Stabilization of the arc is advantageous in increasing the penetration depth. That is, the following formula (2) ′ can be applied instead of the above formula (2), and the following formula (3) ′ can be applied instead of the above formula (3).
  • the base gas of the shielding gas can be Ar gas as in the conventional case. He gas or Ar + He mixed gas may be used. The purity of those base gases may be set to the same level as before.
  • ⁇ ⁇ Welding heat input may be set to an optimum value according to the plate thickness. If the welding heat input is too low, the welding may be insufficient and the weld bead may be discontinuous. Conversely, if the welding heat input is excessive, spatter is likely to occur.
  • an appropriate value of welding heat input can be found in the range of 2000 to 12000 J / cm.
  • the welding heat input is set in the range of 2000 to 4500 J / cm. More preferably.
  • the shield gas flow rate may be adjusted in the range of 10 to 30 L / min. Conventional welding devices can be used.
  • Example 1 The molten Zn—Al—Mg-based plated steel sheet shown in Table 1 was placed horizontally, and a weld bead was formed on the steel sheet surface by an arc generated from a horizontally moving welding torch (bead on plate). The welding conditions are listed in Table 1. The cross section perpendicular to the bead direction including the weld bead and the base material in the vicinity thereof is mirror-polished and etched with a nitric acid solution with a nitric acid concentration of 0.2% by volume. By observing the vicinity, the plating layer evaporation region length indicated by the symbol L in FIG. 5 was measured.
  • FIG. 6 the case where the plating layer evaporation region length is 0.3 mm or more is plotted with a circle mark, and the case where it is less than 0.3 mm is plotted with a cross mark.
  • the CO 2 concentration in the shielding gas is more preferably 5.0% by volume or more, but even in that case, the welding heat input Q is, for example, 2000 to 11500 J / cm. Can be set in a wide range, and can correspond to various plate thicknesses.
  • Example 2 A hot-dip Zn—Al—Mg-based plated steel sheet (thickness of the plating original sheet 2.6 mm) shown in Table 1-2 was placed horizontally, and a weld bead was formed on the steel sheet surface by an arc generated from a horizontally moving welding torch ( Bead on plate). The welding conditions are listed in Table 1-2. By observing the vicinity of the bead toe in the same manner as in Experimental Example 1 described above, the plating layer evaporation region length indicated by the symbol L in FIG.
  • FIG. 8 shows the result.
  • the case where the plating layer evaporation region length is 0.3 mm or more is plotted with a circle mark, and the case where it is less than 0.3 mm is plotted with a mark x.
  • the allowable upper limit is greatly relaxed. As the plate thickness decreases, the cooling rate after welding increases, so that the metal of the plated layer that has become molten after passing through the arc tends to solidify before spreading into the plated layer evaporation region.
  • the allowable upper limit of the CO 2 concentration when the plating layer evaporation region length is 0.3 mm is considered to vary greatly.
  • a molten Zn—Al—Mg based plated steel sheet member is applied to at least one of both members joined by arc welding.
  • Various steel types can be adopted as the plating base plate of the molten Zn—Al—Mg based steel plate member depending on the application. High tensile steel plates can also be used.
  • the thickness of the plating original plate may be 1.0 to 6.0 mm, and may be controlled in the range of 2.0 to 5.0 mm. If the plate thickness of the plating original plate is 2.6 mm or less (for example, 1.0 to 2.6 mm), equation (3) can be applied instead of equation (2).
  • the composition of the molten Zn—Al—Mg based plating layer is, by mass, Al: 1.0 to 22.0%, Mg: 0.05 to 10.0%, Ti: 0 to 0.10. %, B: 0 to 0.05%, Si: 0 to 2.0%, Fe: 0 to 2.5%, the balance Zn and inevitable impurities.
  • the plating layer composition substantially reflects the hot-dip plating bath composition.
  • the method of hot dipping is not particularly limited, it is generally advantageous in terms of cost to use an in-line annealing type hot dipping equipment.
  • the component elements of the plating layer will be described. “%” Of the plating layer component element means “mass%” unless otherwise specified.
  • Al is effective in improving the corrosion resistance of the plated steel sheet and suppresses the generation of Mg oxide dross in the plating bath. In order to fully exhibit these actions, it is necessary to secure an Al content of 1.0% or more, and it is more preferable to secure an Al content of 4.0% or more. On the other hand, when the Al content increases, a brittle Fe—Al alloy layer is likely to grow on the base of the plating layer, and excessive growth of the Fe—Al alloy layer causes a decrease in plating adhesion. As a result of various studies, the Al content is more preferably 22.0% or less, and may be controlled to 15.0% or less, or even 10.0% or less.
  • Mg exhibits the effect of significantly increasing the corrosion resistance of the plated steel sheet by generating a uniform corrosion product on the surface of the plated layer.
  • the Mg content is more preferably 0.05% or more, and more preferably 1.0% or more.
  • Mg oxide-based dross is likely to occur, which causes a reduction in the quality of the plating layer.
  • the Mg content is desirably in the range of 10.0% or less.
  • Ti and B are contained in the hot dipping bath, there are advantages such as an increase in the degree of freedom of manufacturing conditions during hot dipping. For this reason, 1 type or 2 types of Ti and B can be added as needed. It is more effective to add 0.0005% or more in the case of Ti and 0.0001% or more in the case of B. However, when the content of Ti or B in the plating layer is excessive, it causes a poor appearance of the plating layer surface due to the formation of precipitates. When these elements are added, it is desirable that Ti: 0.10% or less and B: 0.05% or less.
  • Si When Si is contained in the hot dipping bath, excessive growth of the Fe—Al alloy layer formed at the interface between the plating original plate surface and the plating layer is suppressed, and the workability of the hot-dip Zn—Al—Mg plated steel sheet is improved. This is advantageous. Therefore, Si can be contained as necessary. In that case, it is more effective to set the Si content to 0.005% or more. However, since excessive Si content causes an increase in the dross amount in the hot dipping bath, the Si content is preferably 2.0% or less.
  • the Fe content in the Zn—Al—Mg plating layer is preferably 2.5% or less.
  • the coating amount of the molten Zn—Al—Mg based steel sheet member is small, it is disadvantageous for maintaining the corrosion resistance and sacrificial anticorrosive action of the plated surface over a long period of time.
  • the Zn—Al—Mg-based plating adhesion amount per side should be 20 g / m 2 or more. It is effective.
  • the plating adhesion amount increases, blow holes are likely to occur during welding. When blow holes occur, the welding strength decreases. For this reason, it is desirable that the amount of plating deposited on one side be 250 g / m 2 or less.
  • the mating member to be joined to the above molten Zn—Al—Mg plated steel sheet member by arc welding may be the same molten Zn—Al—Mg plated steel sheet member as described above, or other steel materials. It doesn't matter.
  • Example 1 A cold-rolled steel strip having a thickness of 3.2 mm and a width of 1000 mm having the composition shown in Table 2 is used as a plating base plate, and this is passed through a hot dipping line to obtain a molten Zn—Al—Mg system having various plating layer compositions. A plated steel sheet was produced. Each shielded Zn—Al—Mg plated steel sheet was subjected to gas shield arc welding by the following test method, and the influence of the shielding gas composition on the resistance to molten metal embrittlement cracking was investigated. The plating layer composition, the plating adhesion amount, and the shielding gas composition are shown in Table 4 below.
  • the composition of the shielding gas applied to the examples of the present invention is composed of at least one of CO 2 : 0 to 16% by volume and the balance: Ar and He (the same applies to Examples 2 and 3 described later).
  • a steel bar boss (protrusion) 15 having a diameter of 20 mm and a length of 25 mm is vertically set up at the center of a 100 mm ⁇ 75 mm test piece 14 (a molten Zn—Al—Mg based plated steel plate member).
  • the test piece 14 and the boss 15 were joined by gas shield arc welding under the welding conditions shown in FIG. Specifically, the boss 15 is rotated once around the boss 15 clockwise from the welding start point S, and after the welding start point S is passed, welding is further performed by overlapping the beads, and an overlapping portion 17 of the weld bead 16 is generated. Welding was performed up to a later welding end point E. During welding, the test piece 14 was held on a flat plate. This test was conducted in a situation where welding cracks are likely to occur experimentally.
  • molten metal embrittlement cracking was observed in the comparative example in which the CO 2 concentration in the shielding gas exceeded the definition of the present invention.
  • the plating layer evaporation region length L (see FIG. 3) in the test piece 14 is less than 0.3 mm, and the deepest molten metal embrittlement crack has a distance from the toe portion of most samples of about 0.3 mm. It occurred at a site within 3 mm.
  • no molten metal embrittlement cracking was observed in the examples of the present invention in which the CO 2 concentration in the shielding gas was limited within the range satisfying the above expression (2).
  • the plating layer evaporation region length L in the examples of the present invention was 0.3 mm or more.
  • Example 2 A cold-rolled steel strip with a thickness of 4.5 mm having the composition shown in Table 2 is used as a plating base plate, and this is passed through a hot dipping line to produce hot-dip Zn—Al—Mg-based plated steel plates having various plating layer compositions. did. Using each molten Zn—Al—Mg plated steel sheet, the influence of the shielding gas composition on the resistance to molten metal embrittlement cracking was investigated by the same evaluation method as in Example 1. The results are shown in Table 5. The plating layer composition, plating adhesion amount, and shielding gas composition are shown in Table 5.
  • the composition of the shielding gas applied to the examples of the present invention consists of one or more of CO 2 : 0 to 7% by volume and the balance: Ar and He.
  • Example 3 A cold-rolled steel strip with a thickness of 6.0 mm having the composition shown in Table 2 is used as a plating base plate, and this is passed through a hot dipping line to produce hot-dip Zn-Al-Mg plated steel plates having various plating layer compositions. did.
  • the influence of the shielding gas composition on the resistance to molten metal embrittlement cracking was investigated by the same evaluation method as in Example 1. The results are shown in Table 6.
  • the plating layer composition, plating adhesion amount, and shielding gas composition are shown in Table 6.
  • the composition of the shielding gas applied to the examples of the present invention is composed of one or more of CO 2 : 0 to 6% by volume and the balance: Ar and He.
  • Example 4 A cold-rolled steel strip with a thickness of 2.6 mm having the composition shown in Table 2 is used as a plating original plate, and this is passed through a hot dipping line to produce hot-dip Zn-Al-Mg plated steel plates having various plating layer compositions. did. Using each molten Zn—Al—Mg plated steel sheet, the influence of the shielding gas composition on the resistance to molten metal embrittlement cracking was investigated by the same evaluation method as in Example 1. The results are shown in Table 7. The plating layer composition, plating adhesion amount, and shielding gas composition are shown in Table 7.
  • the composition of the shielding gas applied to the example of the present invention is composed of one or more of CO 2 : 0 to 17% by volume and the balance: Ar and He.
  • Example 5 A cold rolled steel strip with a thickness of 1.6 mm having the composition shown in Table 2 is used as a plating base plate, and this is passed through a hot dipping line to produce hot-dip Zn-Al-Mg plated steel plates having various plating layer compositions. did. Using each molten Zn—Al—Mg plated steel sheet, the influence of the shielding gas composition on the resistance to molten metal embrittlement cracking was investigated by the same evaluation method as in Example 1. The results are shown in Table 8. The plating layer composition, plating adhesion amount, and shielding gas composition are shown in Table 8.
  • the composition of the shielding gas applied to the example of the present invention is composed of one or more of CO 2 : 0 to 17% by volume and the balance: Ar and He.

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  • Engineering & Computer Science (AREA)
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  • Mechanical Engineering (AREA)
  • Materials Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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EP13803668.6A EP2862662B1 (en) 2012-06-14 2013-05-22 Process for producing arc-welded structural member
RS20171171A RS56575B1 (sr) 2012-06-14 2013-05-22 Postupak proizvodnje elektrolučno zavarenog strukturnog elementa
KR20147027115A KR20150024302A (ko) 2012-06-14 2013-05-22 아크 용접 구조 부재의 제조법
BR112014029946-3A BR112014029946B1 (pt) 2012-06-14 2013-05-22 Método para produzir elemento estrutural de arco soldado
US14/406,569 US20150136741A1 (en) 2012-06-14 2013-05-22 Method for producing arc-welded structural member
SG11201406046YA SG11201406046YA (en) 2012-06-14 2013-05-22 Process for producing arc-welded structural member
MYPI2014703682A MY181348A (en) 2012-06-14 2013-05-22 Process for producing arc-welded structural member
CA2874217A CA2874217A1 (en) 2012-06-14 2013-05-22 Method for producing arc-welded structural member
MX2014010630A MX362408B (es) 2012-06-14 2013-05-22 Metodo para producir miembro estructural soldado por arco.
NZ629861A NZ629861A (en) 2012-06-14 2013-05-22 Method for producing arc-welded structural member
CN201380022431.1A CN104334308B (zh) 2012-06-14 2013-05-22 电弧焊接结构构件的制造方法
AU2013275476A AU2013275476B2 (en) 2012-06-14 2013-05-22 Method for Producing Arc-Welded Structural Member
RU2015100899A RU2635581C2 (ru) 2012-06-14 2013-05-22 Способ для производства сваренного дуговой сваркой конструктивного элемента
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Families Citing this family (10)

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Publication number Priority date Publication date Assignee Title
JP6023156B2 (ja) 2014-11-27 2016-11-09 日新製鋼株式会社 Ｚｎ系めっき鋼板のアーク溶接方法
JP6114785B2 (ja) * 2015-05-29 2017-04-12 日新製鋼株式会社 溶接部外観と溶接強度に優れた溶融Ｚｎ系めっき鋼板のアーク溶接方法、および溶接部材の製造方法
WO2016194400A1 (ja) * 2015-05-29 2016-12-08 日新製鋼株式会社 溶接部外観と溶接強度に優れた溶融Ｚｎ系めっき鋼板のアーク溶接方法、溶接部材の製造方法および溶接部材
JP7257955B2 (ja) 2016-08-08 2023-04-14 コロラド・スクール・オブ・マインズ 低い液相線温度を有する改変された溶融亜鉛めっき被膜、その製造方法及び使用方法
JP6385411B2 (ja) 2016-10-28 2018-09-05 日新製鋼株式会社 溶接部材およびその製造方法
WO2018155508A1 (ja) * 2017-02-22 2018-08-30 日新製鋼株式会社 Ｍｉｇろう付け方法、重ね継手部材の製造方法、および重ね継手部材
EP3587614B8 (en) 2017-02-22 2021-01-20 Nippon Steel Corporation Laser brazing method and production method for lap joint member
JP2021042419A (ja) * 2019-09-10 2021-03-18 日本電産株式会社 亜鉛合金及びその製造方法
CN111545871B (zh) * 2020-04-27 2021-07-13 招商局重工（江苏）有限公司 一种薄板分段大组缝焊接工艺
CN113751840A (zh) * 2021-09-02 2021-12-07 唐山钢铁集团有限责任公司 改善锌铝镁镀层板熔化极气体保护焊焊缝质量的方法

Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3149129B2 (ja) 1997-03-04 2001-03-26 日新製鋼株式会社 耐食性および表面外観の良好な溶融Ｚｎ−Ａｌ−Ｍｇ系めっき鋼板およびその製造法
JP3179401B2 (ja) 1996-12-13 2001-06-25 日新製鋼株式会社 耐食性および表面外観の良好な溶融Ｚｎ−Ａｌ−Ｍｇめっき鋼板およびその製造法
JP2004090017A (ja) * 2002-08-30 2004-03-25 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板のアーク溶接方法
JP2004344905A (ja) * 2003-05-21 2004-12-09 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板の溶融溶接方法
JP2004344904A (ja) * 2003-05-21 2004-12-09 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板の溶融溶接方法
JP2005000986A (ja) * 2003-05-21 2005-01-06 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板の溶融溶接方法
JP2005230912A (ja) 2004-01-22 2005-09-02 Nippon Steel Corp 耐液体金属脆化割れ性に優れたアーク溶接用フラックス入りワイヤおよびアーク溶接方法
JP3715220B2 (ja) 2001-06-22 2005-11-09 日新製鋼株式会社 耐食性に優れたＺｎ−Ａｌ−Ｍｇ系溶融めっき鋼材
JP2009012027A (ja) * 2007-07-03 2009-01-22 Taiyo Nippon Sanso Corp 亜鉛めっき鋼板のｍａｇ溶接用シールドガスおよびこのシールドガスを使用した溶接方法
JP4475787B2 (ja) 2000-10-06 2010-06-09 日新製鋼株式会社 Ｚｎ−Ａｌ−Ｍｇ合金めっき鋼管及びその製造方法
JP2010221247A (ja) * 2009-03-23 2010-10-07 Nippon Steel Corp 接合部の耐食性に優れた亜鉛系合金めっき鋼板の接合継手
JP2011208264A (ja) * 2010-03-30 2011-10-20 Nisshin Steel Co Ltd 耐食性に優れる自動車シャシ部材およびその製造法

Family Cites Families (11)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3679866A (en) * 1969-06-10 1972-07-25 Kobe Steel Ltd Pulsed arc spray welding in a narrow groove
CA2076201C (en) * 1992-08-14 2000-05-16 Grant Harvey Shielding gases for arc welding
JP2001096368A (ja) * 1999-09-27 2001-04-10 Nippon Steel Corp 高強度鋼板のアーク溶接方法
US20090014419A1 (en) * 2001-03-29 2009-01-15 Global Steel, Llc Modular steel concrete reinforcement system
RU2233466C2 (ru) * 2001-06-22 2004-07-27 Новиков Олег Михайлович Регулятор подачи жидкостей и газов
FR2898529B1 (fr) * 2006-03-15 2008-04-25 Air Liquide Soudo-brasage de pieces en acier avec fil en cuivre et melange gazeux oxydant
FR2903623B1 (fr) * 2006-07-12 2008-09-19 L'air Liquide Procede de soudage hybride laser-arc de pieces metalliques aluminiees
JP2010046708A (ja) * 2008-08-25 2010-03-04 Taiyo Nippon Sanso Corp ミグ溶接用シールドガスおよびインバーのミグ溶接方法
US20110318606A1 (en) * 2009-03-10 2011-12-29 Nisshin Steel Co., Ltd. Zinc-based alloy-plated steel material excellent in resistance to molten-metal embrittlement cracking
JP2011043334A (ja) * 2009-08-19 2011-03-03 Tabuchi Electric Co Ltd Ａｃ入力監視回路および電源装置
AU2012224032B2 (en) * 2011-02-28 2017-03-16 Nisshin Steel Co., Ltd. Steel sheet hot-dip-coated with Zn-Al-Mg-based system, and process of manufacturing same

Patent Citations (12)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
JP3179401B2 (ja) 1996-12-13 2001-06-25 日新製鋼株式会社 耐食性および表面外観の良好な溶融Ｚｎ−Ａｌ−Ｍｇめっき鋼板およびその製造法
JP3149129B2 (ja) 1997-03-04 2001-03-26 日新製鋼株式会社 耐食性および表面外観の良好な溶融Ｚｎ−Ａｌ−Ｍｇ系めっき鋼板およびその製造法
JP4475787B2 (ja) 2000-10-06 2010-06-09 日新製鋼株式会社 Ｚｎ−Ａｌ−Ｍｇ合金めっき鋼管及びその製造方法
JP3715220B2 (ja) 2001-06-22 2005-11-09 日新製鋼株式会社 耐食性に優れたＺｎ−Ａｌ−Ｍｇ系溶融めっき鋼材
JP2004090017A (ja) * 2002-08-30 2004-03-25 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板のアーク溶接方法
JP2004344905A (ja) * 2003-05-21 2004-12-09 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板の溶融溶接方法
JP2004344904A (ja) * 2003-05-21 2004-12-09 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板の溶融溶接方法
JP2005000986A (ja) * 2003-05-21 2005-01-06 Nisshin Steel Co Ltd Ｚｎ系めっき鋼板の溶融溶接方法
JP2005230912A (ja) 2004-01-22 2005-09-02 Nippon Steel Corp 耐液体金属脆化割れ性に優れたアーク溶接用フラックス入りワイヤおよびアーク溶接方法
JP2009012027A (ja) * 2007-07-03 2009-01-22 Taiyo Nippon Sanso Corp 亜鉛めっき鋼板のｍａｇ溶接用シールドガスおよびこのシールドガスを使用した溶接方法
JP2010221247A (ja) * 2009-03-23 2010-10-07 Nippon Steel Corp 接合部の耐食性に優れた亜鉛系合金めっき鋼板の接合継手
JP2011208264A (ja) * 2010-03-30 2011-10-20 Nisshin Steel Co Ltd 耐食性に優れる自動車シャシ部材およびその製造法

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